US4761262A - Sintering method - Google Patents

Sintering method Download PDF

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US4761262A
US4761262A US06/928,220 US92822086A US4761262A US 4761262 A US4761262 A US 4761262A US 92822086 A US92822086 A US 92822086A US 4761262 A US4761262 A US 4761262A
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powder
sintering
thermit
pressure
mixture
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Masaru Ogata
Shuichi Takeda
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KOMATSU SEISAKUSHO 3-6 AKASAKA 2-CHOME MINATO-KU TOKYO 107 JAPAN KK
Komatsu Ltd
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Komatsu Ltd
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Assigned to KABUSHIKI KAISHA KOMATSU SEISAKUSHO, 3-6, AKASAKA 2-CHOME, MINATO-KU, TOKYO 107, JAPAN reassignment KABUSHIKI KAISHA KOMATSU SEISAKUSHO, 3-6, AKASAKA 2-CHOME, MINATO-KU, TOKYO 107, JAPAN ASSIGNMENT OF ASSIGNORS INTEREST. Assignors: OGATA, MASARU, TAKEDA, SHUICHI
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J3/00—Processes of utilising sub-atmospheric or super-atmospheric pressure to effect chemical or physical change of matter; Apparatus therefor
    • B01J3/06—Processes using ultra-high pressure, e.g. for the formation of diamonds; Apparatus therefor, e.g. moulds or dies
    • B01J3/062—Processes using ultra-high pressure, e.g. for the formation of diamonds; Apparatus therefor, e.g. moulds or dies characterised by the composition of the materials to be processed
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/02—Compacting only
    • B22F3/08—Compacting only by explosive forces
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/64—Burning or sintering processes
    • C04B35/645—Pressure sintering
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/64—Burning or sintering processes
    • C04B35/65—Reaction sintering of free metal- or free silicon-containing compositions
    • C04B35/651—Thermite type sintering, e.g. combustion sintering
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J2203/00—Processes utilising sub- or super atmospheric pressure
    • B01J2203/06—High pressure synthesis
    • B01J2203/0605—Composition of the material to be processed
    • B01J2203/0645—Boronitrides
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J2203/00—Processes utilising sub- or super atmospheric pressure
    • B01J2203/06—High pressure synthesis
    • B01J2203/065—Composition of the material produced
    • B01J2203/066—Boronitrides
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J2203/00—Processes utilising sub- or super atmospheric pressure
    • B01J2203/06—High pressure synthesis
    • B01J2203/0675—Structural or physico-chemical features of the materials processed
    • B01J2203/0685—Crystal sintering

Definitions

  • This invention relates to a method for the sintering a metal powder, a ceramic powder, or a mixture of a metal powder with a ceramic powder, and more particularly to a sintering method which comprises heating the aforementioned powder by means of Thermit reaction while keeping the powder under pressure.
  • the so-called sintering method which uses a powder as a starting material and converts it into a mass by sintering has heretofore been widely used on metals, ceramics, and composite materials thereof.
  • the largest task imposed on the sintering method consists in obtaining a mass which is compact and is formed of minute crystal grains.
  • pressure sintering methods resorting as to a hot press and a hot hydrostatic press are available. They use pressures on the order of 500 atmospheres and 2,000 atmospheres respectively.
  • For the heating to be made under a still higher pressure it is necessary to use such an apparatus for the generation of ultrahigh pressure and high temperature as disclosed in Japanese Patent Publication SHO 36(1961)-23,463, for example. With this apparatus, sintering can be carried out under not less than 10,000 atmospheres of pressure.
  • the apparatus Since a heater installed outside the material under treatment or resistance heating caused by passage of electricity to the material under treatment itself is utilized for the heating, the apparatus requires a power source of a large capacity.
  • An object of the invention is to provide, for elimination of disadvantages of the prior art, a method for sintering a metal powder, a ceramic powder, or a mixture thereof which attains intimate sintering of even a high melting substance by carrying out a high-temperature heating under ultrahigh pressure for a short time.
  • Another object of this invention is to provide a sintering method which comprises heating a metal powder, a ceramic powder, or a mixture thereof as kept under pressure with the heat of a Thermit reaction.
  • Yet another object of this invention is to provide a method for sintering a metal powder, a ceramic powder, or a mixture thereof, wherein the sintered article to be produced is protected so as not to be corroded by the product of Thermit reaction.
  • the first embodiment of this invention provides a method for sintering a metal powder, a ceramic powder, or a mixture thereof by heating the aforementioned powder or mixture as held under pressure with the heat of Thermit reaction.
  • the second embodiment of this invention provides a sintering method set forth in the first embodiment mentioned above, which further comprises interposing a barrier made of hexagonal boron nitride and/or tantalum between the powder subjected to sintering and a Thermit composition.
  • the third embodiment of this invention provides a sintering method set forth in the first embodiment mentioned above, which further comprises disposing a Thermit composition around the entire periphery of the powder subjected to sintering, heating the powder with the heat generated by the Thermit reaction and, at the same time, fusing a part or the whole of the product of the Thermit reaction thereby hydrostatically applying pressure on the powder.
  • the fourth embodiment of this invention provides a sintering method set forth in any of the first through third embodiments mentioned above, wherein the Thermit composition is a mixture of iron oxide powder with aluminum powder, a mixture of iron oxide powder with silicon powder, or a mixture of iron oxide powder with aluminum powder and silicon powder.
  • the fifth embodiment of this invention is a sintering method set forth in the first embodiment mentioned above, wherein the pressure resulting from the Thermit reaction is not less than 10,000 atmospheres.
  • the sixth embodiment of this invention provides a sintering method set forth in any of the first through fifth embodiments mentioned above, wherein the powder subjected to sintering is one member or a mixture of at least two members selected from among TiB 2 , ZrB 2 , and HfB 2 , or one member or a mixture of at least two members selected from among the compounds based on the aforementioned borides.
  • the seventh embodiment of this invention provides a sintering method set forth in the first embodiment mentioned above, wherein the powder subjected to sintering has a grain size of not more than 1 ⁇ m.
  • the eighth embodiment of this invention provides a sintering method set forth in the first embodiment described above, wherein the powder of one member or a mixture of at least two members selected from among TiB 2 , ZrB 2 , and HfB 2 is sintered as held under pressure with the heat of the reaction of a Thermit composition to produce a heat-resistant, abrasion-resistant, electroconductive, and neutron-shielding high-density sintered article.
  • the ninth embodiment of this invention provides a sintering method set forth in the eighth embodiment mentioned above, wherein the pressure resulting from the Thermit reaction is not less than 10,000 atmospheres.
  • the accompanying drawing is a partially cutaway schematic longitudinal cross section illustrating the layout of an assembly in an ultrahigh pressure apparatus as a typical means of accomplishing the sintering method of this invention.
  • the so-called Thermit reaction i.e. a chemical reaction that generates the heat capable of accomplishing quick high-temperature heating, is utilized.
  • the powder By disposing a Thermit composition around the periphery of a powder subjected to sintering, the powder can be heated in an extremely short time. Further, by the reaction, the Thermit composition is fused to cause hydrostatic application of pressure on the powder. Moreover, since the heating is completed in an extremely small time, the refractory used for retaining the Thermit composition can withstand the high-temperature heating which is never realized by the conventional resistance heating.
  • the heating temperature can be adjusted by varying the charging amount, the percentage composition, or the kind of the Thermit composition.
  • the powder of Si, Ti, Mg, or Ca for example, can be used instead of that of Al.
  • FeO, Fe 3 O 4 , or other similar oxide having a small free energy of formation can be used in the place of Fe 2 O 3 .
  • the combination of an oxide with a metal is no exclusive requirement. It is permissible to combine a carbide, nitride, or boride powder having a small free energy of formation with a metal powder capable of reducing the powder just mentioned. It should be noted, however, that a composition which produces a large heat from a chemical reaction but which produces a gaseous phase like an explosive cannot be used because it generates a notably high pressure at the same time.
  • a layer of hexagonal boron nitride or tantalum, for example, is desired to be interposed for the purpose of preventing the sintered article from being corroded by the product of the Thermit reaction.
  • the ignition of Thermit is effected by passing electricity to the Thermit composition or to a separately disposed heater thereby heating part or the whole of the Thermit composition.
  • Thermit composition consisting of 1 mol of Fe 2 O 3 and 2 mols of Al is kept under 20,000 atmospheres of pressure, it is ignited as part thereof is heated to about 830° to 1,000° C.
  • FIG. 1 illustrates the condition of disposition in the ultrahigh pressure generating apparatus.
  • Reference numerals 1, 2 denote a cylinder and an anvil respectively which form an ultrahigh pressure generating vessel.
  • Numeral 3 denotes a gasket made of pyrophyllite and adapted to seal in pressure.
  • Numeral 4 denotes a heat insulator made of pyrophyllite.
  • a copper plate 5, a ring 6 made of steel, a steel plate (or molybdenum plate) 7, and a ceramic heat insualtor 8 jointly form an assembly for feeding electricity to a cylindrical graphite heater 9.
  • the Thermit composition was spontaneously ignited at the time that the temperature of the sample chamber reached 920° C.
  • the ignition of Thermit can be easily detected by a decrease of electric resistance due to a sharp rise of temperature because the temperature coefficient of electric resistance of the graphite heater is a negative number.
  • the ignition can also be detected by a decrease of distance between the anvils due to ignition of Thermit.
  • Thermit reaction completed itself in less than 1 second. The sample part was left standing under the existing pressure for 5 minutes, then cooled, relieved of the pressure, and opened to permit recovery of TiB 2 .
  • the former TiB 2 powder was already converted into a perfectly compact sintered article, which was found to have a relative density of not less than 99% as measured by the Archimedean method. None of the sintered articles of pure TiB 2 so far produced has acquired such a high compactness as this.
  • Example 1 It was confirmed by an electroconductivity test that the sintered article of TiB 2 obtained in Example 1 was a specific ceramic piece exhibiting the same degree of electroconductivity as a metal. It was readily fabricable by electron discharge cutting.
  • This sintered article was extremely hard, exhibiting a Knoop hardness of 4,100 kg/mm 2 , and could easily inflict a scratch on hard metal.
  • Example 2 A test was conducted by following the procedure of Example 1, except that the amount of the Thermit composition was changed to 36.7 g and the pressure to 10,000 atmospheres. The amount of heat generated by the Thermit reaction was about 35 Kcal, supporting an estimate that the heating proceeded to a temperature exceeding the melting point of TiB 2 (2,980° C. by the known data). In this example, too, the TiB 2 powder was converted into a compact sintered article.
  • HfB 2 powder made by Cerac Inc.
  • the HfB 2 was converted into a compact sintered article, which exhibited a satisfactory electroconductivity. It was confirmed to possess high hardness enough to inflict a scratch on hard metal.
  • a sintering test was carried out by following the procedure of Example 1, except that 11.3 g of ZrB 2 powder (made by Cerac Inc.) having grain sizes of not more than 325 mesh and 24 g of a Thermit composition consisting of Fe 2 O 3 and Al in a molar ratio of 1/2 were used instead.
  • the amount of heat generated by the reaction was about 23 Kcal, supporting an estimate that the highest temperature reached by the sample part was 2,640° C.
  • the ZrB 2 ws converted into a compact sintered article having a gray metallic gloss. It was a good conductor of electricity. This sintered article had a fine texture showing no sign of crystal grain growth and possessed high hardness enough to inflict readily a scratch on hard metal.
  • Example 5 From the sintered article obtained in Example 5, a bar 1.5 mm in thickness, 3 mm in width, and 20 mm in length was cut by the use of an NC type wire cutting device adopting the principle of electron discharge cutting. This cutting was as easy as in wire cutting of hard metal. The cut surface was flat and smooth.
  • the present sintered article excels in electron discharge machinability. In this respect the sintered article proves highly useful commercially.
  • the sintered article consequently obtained was a compact disc 11.7 mm in diameter, indicating that the molded powder had shrunken in the radial direction.
  • the material under treatment slightly expands from its original diameter in the radial direction perpendicular to the direction of pressure application.
  • the radial shrinkage observed in the radial direction implies that the Thermit composition disposed around the periphery of the disc was fused by ignition and allowed to exert hydrostatic pressure.
  • the sintered article consequently obtained had a relative density of not less than 97%. By an X-ray diffraction, this sintered article was found to have undergone thorough phase transformation to ⁇ crystals.
  • Example 2 A test was carried out by faithfully following the procedure of Example 1, except that the amount of the Thermit composition was doubled. Consequently, there was obtained a sintered article having a relative density of not less than 97%.
  • An X-ray diffraction of a cross section of this sintered article revealed occurrence of a ⁇ phase and an ⁇ phase both in fairly high percentages.
  • the ⁇ phase is a stable structure at low temperatures and the ⁇ phase at high temperatures. The occurrence of these two phases indicates that although the amount of heat generated in this example was larger than in Example 7, the sample part reached a lower temperature.
  • a sintering test was carried out under 20,000 atmospheres of pressure, using 9 g of a mixture consisting of 5% by weight of Y 2 O 3 , 3% by weight of Al 2 O 3 , and the balance of Si 3 N 4 and 96.7 g of a Thermit composition consisting of Fe 2 O 3 and Al in a molar ratio of 1/2 as disposed in the same manner as in Example 1. Consequently, there was obtained a sintered disc. The hardness of this disc measured on the surface thereof was 1,950 kg/mm 2 by the Vickers scale.
  • Si 3 N 4 can be sintered under atmospheric pressure by the use of a sintering aid such as Y 2 O 3 , Al 2 O 3 , or MgO.
  • a sintered article of the same composition as used in this example obtained in an atmosphere of nitrogen under 1 atmosphere of pressure at 1,750° C. has a Vickers hardness in the range of 1,300 to 1,400 kg/mm 2 . Comparison shows that the method of this invention notably enhances the hardness.
  • the KIC of the sintered article as determined by the so-called micro-indentation method which measures toughness at rupture by the length of a crack produced from the corner of a pressure mark inflicted during the Vickers hardness test under a large load, was 1 to 10 MNm - 3/2, a toughness about twice the toughness, 4.5 to 5.5 MNm - 3/2, of the sintered article produced under the atmospheric pressure.
  • Si 3 N 4 When Si 3 N 4 is sintered in the presence of a sintering aid as in the present example, since the sintering occurs in a liquid phase, crystal grains attain a notable growth. For example, even when the primary grain size of Si 3 N 4 is 0.5 ⁇ m, the Si 3 N 4 grains of the sintered article attain growth to about 5 to 10 times the original grain size. This is a phenomenon which occurs both under atmospheric pressure and ultrahigh pressure.
  • the high hardness and the high toughness described above may be ascribable to the effect of the method of this invention manifested in increasing the density beyond the level obtainable by the atmospheric sintering and suppressinggrowth of crystal grains.
  • the amount of heat generated by the Thermit reaction was 16 Kcal.
  • the rate of the reaction was lower than when the Thermit composition used Al.
  • the material under treatment was left standing under the existing pressure for 5 minutes following the ignition and then relieved of the pressure. Consequently, there was obtained a compact sintered article of high speed steel.
  • the relative density of this sintered article was 100%.
  • a ferrite type stainless steel powder composed of 18% by weight of Fe, 2% by weight of Cr, and the balance of Mo and 2% by volume of ⁇ -alumina particles of not more than 0.1 ⁇ m were mixed for 20 hours to comminute the ferrite crystal grains to less than 1 ⁇ m and effect uniform dispersion of alumina.
  • Example 10 In the same apparatus as used in Example 10, 20 g of the resulting mixed powder was positioned, ignited and sintered under 20,000 atmospheres of pressure.
  • the graphite heater of Example 10 was not used. Instead, a Fe-Al alloy wire 1 mm in diameter was inserted through the gasket part and part of the circuit thereof was held in contact with the Thermit composition of Fe 2 O 3 and Si. The ignition was effected by feeding electricity to the Fe-Al alloy wire.
  • the Vickers hardness of the produced sintered article was 860 kg/mm 2 in its sintered state, 310 kg/mm 2 at an elevated temperature of 800° C., and 720 kg/mm 2 after one hour's tempering.
  • the sintered article was formed of extremely minute crystal grains.
  • a specimen of the sintered article was observed under an opticalmicroscope at 1,000 magnifications, neither detection of alumina nor measurement of grain size of stainless steel crystals was easily obtained.
  • the method of this invention permits application of high pressure and a high temperature and, therefore, proves highly effective in sintering high melting ceramics and high melting metals which defy sintering by the conventional method.
  • the working examples cited above illustrate only part of the embodiments of this invention.
  • the method of this invention can be used for the production of sintered articles of ceramics based on the oxides of such elements as Al, Mg, Be, Zr, Y, Th, Ti, Hf, Cr, La, Sm, and Er, the nitrides of such elements as Ti, Zr, Hf, V, Nb, Ta, Al, Si, Th, and U, the carbides of such elements as Ti, Zr, Hf, V, Nb, Ta, Si, W, Mo, and Cr, and the borides of such elements as C, Al, V, Nb, Ta, Ti, Zr, Hf, Sc, and Y.
  • oxides of such elements as Al, Mg, Be, Zr, Y, Th, Ti, Hf, Cr, La, Sm, and Er
  • the nitrides of such elements as Ti, Zr, Hf, V, Nb, Ta, Al, Si, Th, and U
  • the carbides of such elements as Ti, Zr, Hf, V, Nb, Ta, Si
  • the method is also useful as a means of compactly sintering such high melting metals as W and Mo. Further, since the sintering can be effected quickly under a high pressure, the powder can be sintered without entailing growth of crystal grains.
  • the method can produce materials highly useful commerically.
  • TiB 2 , ZrB 2 , and HfB 2 shown in the working examples have never been obtained as high-density sintered articles by the conventional method.
  • these sintered articles can be used in heat-resistant materials, corrosionproof materials, abrasion-resistant materials, and cutting tools.
  • Owing to their outstanding electroconductivity and resistance to heat they can be used in high-temperature heating elements, electric contact materials, and electrode materials. They have a characteristic feature that, owing to satisfactory electroconductivity, they can be machined by electric discharge. Further, since they have large cross section for neutron absorption, they can be utilized as neutron shields in an atomic furnace.
  • the sintered articles of Si 3 N 4 are characterized by high hardness and high toughness and, therefore, have a bright prospect of being used as cutting tools of longer service life than the conventional cutting tools.
  • the high speed steel articles and the grain-dispersed stainless steel articles sintered by the method of this invention are excellent materials for tools.
  • the sintered articles of grain-dispersed stainless steel are useful as corrosionproof and erosionproof materials and as heat-resistant materials.
  • the method of this invention can be applied to sintering of substantially all materials and can produce commercially useful materials.
  • the pressure is desired to be as high as possible. This statement does not necessarily mean that the pressure should be limited to ultrahigh pressure exceeding 10,000 atmospheres specifically. It goes without saying that this invention can be effectively applied to a hot press using a working pressure on the order of several hundreds of kg/cm 2 .
  • the sintering can be carried out under an ultrahigh pressure at a high temperature, the high melting substances which have defied sintering by the conventional method can be be sintered compactly.

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US06/928,220 1985-02-15 1986-02-14 Sintering method Expired - Fee Related US4761262A (en)

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JP60026424A JPH0791567B2 (ja) 1985-02-15 1985-02-15 焼結方法
JP60-026424 1985-02-15

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Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5082540A (en) * 1990-05-07 1992-01-21 The Secretary Of State For Defence In Her Britannic Majesty's Government Of The United Kingdom Of Great Britain And Northern Ireland Fluoride ion sensitive materials
US5302340A (en) * 1988-04-21 1994-04-12 Kabushiki Kaisha Komatsu Seisakusho Method of forming ceramic layer on metallic body
US5422069A (en) * 1992-07-23 1995-06-06 Reading Alloys, Inc. Master alloys for beta 21S titanium-based alloys and method of making same
US5580517A (en) * 1994-11-08 1996-12-03 Kyushu Ceramics Industry Co., Ltd. Method of making composites of metals and oxides
US6168072B1 (en) 1998-10-21 2001-01-02 The Boeing Company Expansion agent assisted diffusion bonding
EP1344592A2 (en) * 2002-03-13 2003-09-17 National Institute for Materials Science Method for sintering tungsten powder
CN101423413B (zh) * 2008-11-27 2011-09-21 中钢集团洛阳耐火材料研究院有限公司 一种制备ZrB2—Al2O3复合粉体的方法
US20110229720A1 (en) * 2010-03-16 2011-09-22 The Boeing Company Method and Apparatus For Curing a Composite Part Layup
US8343402B1 (en) * 2007-09-13 2013-01-01 The Boeing Company Consolidation of composite material
US8556619B2 (en) 2007-09-13 2013-10-15 The Boeing Company Composite fabrication apparatus
US8708691B2 (en) 2007-09-13 2014-04-29 The Boeing Company Apparatus for resin transfer molding composite parts
US9555506B2 (en) 2012-02-28 2017-01-31 Kyocera Corporation Drill blank, method for manufacturing drill blank, drill, and method for manufacturing drill
CN108187588A (zh) * 2018-01-25 2018-06-22 铜仁学院 解决合成金刚石泄压放气炮的叶腊石合成块及其制备方法

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH01119568A (ja) * 1987-10-30 1989-05-11 Univ Osaka 加圧自己燃焼焼結法
JP2717541B2 (ja) * 1988-04-21 1998-02-18 株式会社小松製作所 金属体上へのセラミック層形成方法
JP2538340B2 (ja) * 1989-06-12 1996-09-25 株式会社小松製作所 セラミックス焼結体の製造方法
DE69032117T2 (de) * 1989-06-12 1998-09-17 Komatsu Mfg Co Ltd Verfahren zur herstellung von gesinterten keramischen materialien
JP2002363544A (ja) * 2001-06-04 2002-12-18 Sinto Brator Co Ltd 球状投射材の製造方法及び投射材

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3865573A (en) * 1973-05-23 1975-02-11 Kennecott Copper Corp Molybdenum and ferromolybdenum production
US3909909A (en) * 1971-07-21 1975-10-07 Republic Steel Corp Harmonic press and method of forging
US3999952A (en) * 1975-02-28 1976-12-28 Toyo Kohan Co., Ltd. Sintered hard alloy of multiple boride containing iron
JPS6054272A (ja) * 1983-09-03 1985-03-28 Toyama Hiratsuka Kenkyusho:Kk 切断，穿孔用加工ヘッド
US4610726A (en) * 1984-06-29 1986-09-09 Eltech Systems Corporation Dense cermets containing fine grained ceramics and their manufacture
US4655830A (en) * 1985-06-21 1987-04-07 Tomotsu Akashi High density compacts

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6054272B2 (ja) * 1979-02-15 1985-11-29 黒崎窯業株式会社 耐火物の製造方法
JPH0233676B2 (ja) * 1981-11-28 1990-07-30 Toyota Motor Co Ltd Tankakeiso*kinzokufukugokanoyobisonoseizohoho

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3909909A (en) * 1971-07-21 1975-10-07 Republic Steel Corp Harmonic press and method of forging
US3865573A (en) * 1973-05-23 1975-02-11 Kennecott Copper Corp Molybdenum and ferromolybdenum production
US3999952A (en) * 1975-02-28 1976-12-28 Toyo Kohan Co., Ltd. Sintered hard alloy of multiple boride containing iron
JPS6054272A (ja) * 1983-09-03 1985-03-28 Toyama Hiratsuka Kenkyusho:Kk 切断，穿孔用加工ヘッド
US4610726A (en) * 1984-06-29 1986-09-09 Eltech Systems Corporation Dense cermets containing fine grained ceramics and their manufacture
US4655830A (en) * 1985-06-21 1987-04-07 Tomotsu Akashi High density compacts

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5302340A (en) * 1988-04-21 1994-04-12 Kabushiki Kaisha Komatsu Seisakusho Method of forming ceramic layer on metallic body
US5082540A (en) * 1990-05-07 1992-01-21 The Secretary Of State For Defence In Her Britannic Majesty's Government Of The United Kingdom Of Great Britain And Northern Ireland Fluoride ion sensitive materials
US5422069A (en) * 1992-07-23 1995-06-06 Reading Alloys, Inc. Master alloys for beta 21S titanium-based alloys and method of making same
US5580517A (en) * 1994-11-08 1996-12-03 Kyushu Ceramics Industry Co., Ltd. Method of making composites of metals and oxides
US6168072B1 (en) 1998-10-21 2001-01-02 The Boeing Company Expansion agent assisted diffusion bonding
EP1344592A2 (en) * 2002-03-13 2003-09-17 National Institute for Materials Science Method for sintering tungsten powder
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US10543647B2 (en) 2007-09-13 2020-01-28 The Boeing Company Apparatus for curing a composite part layup
US8343402B1 (en) * 2007-09-13 2013-01-01 The Boeing Company Consolidation of composite material
US8556619B2 (en) 2007-09-13 2013-10-15 The Boeing Company Composite fabrication apparatus
US8708691B2 (en) 2007-09-13 2014-04-29 The Boeing Company Apparatus for resin transfer molding composite parts
CN101423413B (zh) * 2008-11-27 2011-09-21 中钢集团洛阳耐火材料研究院有限公司 一种制备ZrB2—Al2O3复合粉体的方法
US20110229720A1 (en) * 2010-03-16 2011-09-22 The Boeing Company Method and Apparatus For Curing a Composite Part Layup
US8865050B2 (en) 2010-03-16 2014-10-21 The Boeing Company Method for curing a composite part layup
US9555506B2 (en) 2012-02-28 2017-01-31 Kyocera Corporation Drill blank, method for manufacturing drill blank, drill, and method for manufacturing drill
CN108187588A (zh) * 2018-01-25 2018-06-22 铜仁学院 解决合成金刚石泄压放气炮的叶腊石合成块及其制备方法
CN108187588B (zh) * 2018-01-25 2021-05-04 铜仁学院 解决合成金刚石泄压放气炮的叶腊石合成块及其制备方法

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JPH0791567B2 (ja) 1995-10-04
DE3690073T (zh) 1987-04-02

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